WO2018227792A1 - Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor - Google Patents

Abstract

An iron-based amorphous alloy. The iron-based amorphous alloy comprises components Fe_aB_bSi_c, a, b and c respectively indicating atomic percentage contents, 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100. An iron-based amorphous alloy strip is obtained by means of a rapid quenching method in which a single roller is used. Because the iron-based amorphous alloy has higher saturated magnetic induction density, a higher amorphous formation capability and lower stress-resistance sensitivity, the iron-based amorphous alloy can be used as an iron core material for preparing a power transformer, a power generator and an engine; in addition, due to the low stress sensitivity of the iron-based amorphous alloy, the sudden short-circuit resistance capability of an amorphous transformer can be improved when the power transformer is prepared.

Description

Iron-based amorphous alloy with low stress sensitivity and preparation method thereof

This application claims priority from Chinese Patent Application No. 201010447487.1, entitled "A Fe-Based Amorphous Alloy with Low Stress Sensitivity and Its Preparation Method", filed on June 14, 2017, The entire contents of this application are incorporated herein by reference.

Technical field

The invention relates to the technical field of iron-based amorphous alloys, in particular to an iron-based amorphous alloy with low stress sensitivity and a preparation method thereof.

Background technique

Due to its low iron loss, high saturation magnetic flux density, high magnetic permeability and other advantages, Fe-based amorphous alloy ribbons such as Fe-Si-B amorphous alloy ribbons are widely used as cores for power transformers and high frequency transformers. Based on the above characteristics, amorphous iron-based materials have dominated the field of transformers for a long time.

With the continuous renewal of silicon steel materials, the advantages of amorphous materials are relatively weak. For example, the saturation magnetic density of amorphous materials is obviously low, the magnetic induction is low, and the stress sensitivity is poor. In order to improve the saturation magnetic induction and reduce the loss of amorphous materials, amorphous materials have done a lot of work in recent years, but the research on the sensitivity of amorphous materials to stress is not significant. Stress removal is the fundamental guarantee for the low loss characteristics of amorphous materials. In addition, as the main material of the magnetic circuit of the transformer, the thickness of the strip is 20-30μm. Because it is hard and brittle, it is difficult to shear. Therefore, the cross section of the amorphous alloy transformer core is rectangular, and the corresponding high and low voltage windings can only Use a rectangle. The rectangular winding has poor short-circuit resistance with respect to the circular winding, so it is necessary to improve the short-circuit resistance of the amorphous alloy transformer.

The stress of the amorphous transformer core is mainly composed of two parts of stress. One is the internal stress generated by the amorphous material during the preparation process, that is, the quenched internal stress of the amorphous material. On the other hand, the iron core manufacturing process is caused by the iron core structure. Inevitable assembly external stress. A large number of studies have mainly reduced stress from the annealing process and the optimization of the transformer core structure.

The quenching internal stress of amorphous materials is mainly related to the formation of amorphous materials. Rapid cooling is a necessary condition for the formation of amorphous materials. The high temperature melt is poured onto the cooling substrate to form a short-range order at a cooling rate of 10 ⁶ °C/s. Amorphous strip of long-range disordered structure. The short-range disordered structure of the liquid state is "frozen", and internal stress is generated inside these "frozen" structures. The amorphous material can effectively remove the internal stress of the amorphous material through the annealing process, and the amorphous industry has done a lot of work in removing the internal stress. Annealing Removes the internal stress in the quenched state and also causes the thermal stress generated by the large difference in core temperature, that is, the internal stress cannot be completely removed.

The external stress of the assembly is mainly caused by the process of making the core of the amorphous strip during the assembly process of the core and the external stress caused by the structural characteristics of the core itself. The generation of such stress is inevitable, and the research on this part of the stress is relatively small, mainly by the optimization of the transformer core structure and the operation specification. The amorphous alloy transformer winding is a rectangular structure, and the electric power received is far less uniform than the circular winding of the ordinary transformer, and it is more easily deformed when subjected to sudden short-circuit electric power. Since the core material of the amorphous alloy transformer is very sensitive to mechanical stress, both tensile stress and bending stress will affect its performance. Therefore, structural consideration should be taken into consideration to reduce the stress on the core; special fastening measures are generally required. The amorphous alloy transformer body adopts an axial load-bearing structure. The amorphous alloy core and the rectangular winding are not interfered by each other, and the rectangular winding is pressed by the upper and lower clamps and the pressing plate, and the compacted structure is self-contained. Therefore, the test of the short-circuit electric power of the rectangular winding in the axial direction and the radial direction is more severe than that of the circular winding. In order to reduce the assembly and design difficulty of the transformer, it is very important to reduce the stress sensitivity of the amorphous alloy.

For example, JP-A-63-45318 proposes measures for improving the annealing process, mainly by reducing the temperature difference in the core. That is, a method of installing a heat insulating material on the inner and outer surfaces of the core to minimize the temperature difference in the core during cooling, and the like, it is desired to improve the thin strip itself to improve the weight and bulk of the core, and to be heated in the heat treatment furnace, and the core is heated. The more likely each part is to generate temperature unevenness. The method of annealing and de-stressing does not cause crystallization due to excessive temperature of the iron core in the furnace and incomplete stress removal due to too low temperature. However, the specific embodiment of the method is not specifically described herein, and the iron core annealing process and the annealing cost are increased, and the practical annealing process is not practical.

Chinese Patent Publication No. CN1281777C mentions that by adding a specific range of P in a limited composition range of Fe, Si, B, and C, it is found that temperature unevenness occurs in various portions of the core during annealing. Annealing at lower temperatures also shows excellent soft magnetic properties. The inventors only considered the effect of P on reducing the temperature unevenness of the amorphous iron core, and did not consider the problem of oxidation of the phosphorus-containing amorphous ribbon and surface crystallization. The anti-oxidation ability of the P element is extremely poor, and annealing in an aerobic environment is highly susceptible to deterioration of performance due to oxidation and deterioration of apparent quality. For example, in the annealing environment of Fe, Si, B, and C, the phosphorus-containing amorphous material is annealed, and the surface of the strip is blue due to oxidation, and the performance is deteriorated. This has extremely high requirements on the oxygen content of the annealing atmosphere; in addition, there is no preparation of the amorphous ribbon ferrophosphorus at this stage, so that the introduction of the ferrophosphorus will produce unavoidable impurities, which easily causes the problem of surface crystallization of the strip. In summary, the above method avoids the defect of large temperature difference of iron core At the same time, the problems of annealing and oxidation of amorphous ribbon and crystallization of the ribbon are introduced.

U.S. Patent No. US20160172087 discloses a study of the stress release of different compositions, points out the effect of B and C on the degree of stress release, and demonstrates the amount of stress release after strip annealing through an experimental model. This characterization method can explain the stress release of different components to a certain extent, but the inventor only removes the internal stress angle after annealing of the single strip to explain the stress release degree, and does not consider the final soft magnetic properties of the material and the assembly of the transformer core. Deterioration of performance after stress.

As described above, although the embodiment of the above invention example optimizes the annealing process or the amorphous transformer core assembly process, the amorphous ribbon stress can be removed to a greater extent to some extent, but these optimizations are not specifically considered for the strip. The feasibility of preparation and implementation is comprehensively considered, and there is a lack of comprehensive understanding of the destressing (evasion stress) of amorphous ribbons, and the results are relatively one-sided.

Summary of the invention

The technical problem solved by the present invention is to provide an iron-based amorphous alloy strip, and the iron-based amorphous alloy strip provided by the present application has low stress sensitivity.

In view of this, the present application provides an iron-based amorphous alloy as shown in formula (I).

Fe _a B _b Si _c (I);

Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100.

Preferably, the iron-based amorphous alloy has a saturation magnetic induction of ≥1.60T.

Preferably, the atomic percentage of the Fe is 80.0 ≤ a ≤ 81.5.

Preferably, the atomic percentage of the B is 11.0 ≤ b ≤ 12.5.

Preferably, the atomic percentage of the Si is 7.0 ≤ c ≤ 8.0.

Preferably, in the iron-based amorphous alloy, a = 80.0, 12.0 ≤ b ≤ 13.0, and 7.0 ≤ c ≤ 8.0.

Preferably, in the iron-based amorphous alloy, a = 80.5, 11.5 ≤ b ≤ 12.5, and 7.0 ≤ c ≤ 8.0.

Preferably, in the iron-based amorphous alloy, 81.0 ≤ a ≤ 81.5, 11.0 ≤ b ≤ 13.0, 7.0 ≤ c ≤ 8.0.

The application also provides a method for preparing an iron-based amorphous alloy strip as shown in formula (I), comprising:

The element is compounded according to the atomic percentage of the formula (I), and the raw material after the compounding is melted, and the melted molten metal is heated and kept warm, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip;

Fe _a B _b Si _c (I);

Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100.

Preferably, after the single-roll quenching, the method further comprises:

The iron-based amorphous alloy after the single roll quenching is heat-treated.

Preferably, before the heat treatment, the method further comprises: winding a single-roll quenched iron-based amorphous alloy into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and a strain coefficient allowed by loss of the sample ring after heat treatment. For 10.0%, the excitation power allows a strain factor of 6%.

Preferably, the heat-treated iron-based amorphous alloy strip has a coercive force of ≤3.5 A/m; at 50 Hz, 1.35 T, the heat-affected iron-based amorphous alloy strip has a magnetizing power of <0.1450 VA/kg, core loss <0.1100W/kg; at 50Hz, 1.40T, the thermal power of the iron-based amorphous alloy strip after heat treatment is <0.1700VA/kg, core loss <0.1500W/kg .

Preferably, the iron-based amorphous alloy strip is in a completely amorphous state, has a critical thickness of at least 75 μm, and a shear limit strip thickness of at least 29 μm.

The present application provides an iron-based amorphous alloy strip having an atomic composition such as the formula Fe _a B _b Si _c , wherein a, b and c respectively represent the atomic content of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100; Fe in the iron-based amorphous alloy provided by the present application can ensure stable amorphous preparation and higher amorphous ratio Iron-based alloy; Si element is favorable for stable formation of amorphous material; B is the element that contributes the most to alloy amorphization; therefore, the present application makes iron-based amorphous alloy high by adjusting the contents of Fe, Si and B. Saturated magnetic induction and high ductility; at the same time, it also has low stress sensitivity. The iron core prepared by using this alloy has a strong resistance to sudden short circuit.

DRAWINGS

1 is a schematic view showing a simulation experiment device for an unstressed state of an iron-based amorphous alloy sample ring prepared by the present invention;

2 is a schematic view of a simulation test apparatus for applying a stress state to an iron-based amorphous alloy sample ring prepared by the present invention.

detailed description

In order to further understand the present invention, the preferred embodiments of the present invention are described in conjunction with the embodiments of the invention. Limitations of the claims of the present invention.

No matter the internal stress or the external stress is inevitable, the stress is still existed through the optimization of the annealing process, the optimization of the transformer core structure and the specification operation. How to adjust the sensitivity of stress (internal stress, external stress) of different component strips through composition adjustment, establish the range of amorphous components with low stress sensitivity, and effectively present the excellent soft magnetic properties of amorphous products. The amorphous transformer with strong resistance to sudden short circuit is the main purpose of the research of this application. Thus, an embodiment of the invention discloses an iron-based amorphous alloy as shown in formula (I),

Fe _a B _b Si _c (I);

Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100.

The iron-based amorphous alloy provided by the present application contains Fe, Si and B, and has good amorphous forming ability, saturation magnetic induction strength and soft magnetic property by controlling the content of the above elements; further, the present application provides The strip prepared from the iron-based amorphous alloy has low stress sensitivity after heat treatment.

In the iron-based amorphous alloy, Fe is a basic element, and its content is 79.5 ≤ a ≤ 82.5 in terms of atomic percentage. If the atomic percentage of Fe is too low, the saturation magnetic induction density of the iron-based amorphous alloy is too low. The defect of improving the low magnetic density of amorphous can not be obtained, and sufficient magnetic flux density and structurally dense core design cannot be obtained; if the content is too high, the thermal stability of the iron-based amorphous alloy and the formability of the strip are lowered. It is difficult to straighten the strip and a good magnetic product cannot be obtained. In a specific embodiment, the atomic percentage of Fe is 79.5 ≤ a ≤ 81.5, and more specifically, the atomic percentage of Fe is 80.0 ≤ a ≤ 81.5.

The atomic percentage of the Si is 6.5 ≤ c ≤ 8.5, and if the content is too low, the formability of the iron-based amorphous alloy strip and the thermal stability of the amorphous alloy strip are lowered, so that the amorphous material is stably formed. It becomes difficult; when the content is too high, the brittleness of the iron-based amorphous alloy is increased, and the ductility of the strip after annealing is deteriorated. In a specific embodiment, the Si content is 7.0 ≤ c ≤ 8.0.

The atomic percentage of B is 11.0 ≤ b ≤ 13.5, and if the content of B is too low, it becomes difficult to form an amorphous material stably, and if the content is too high, the ability to form an amorphous state is not further advanced. The increase, that is, the B content in the above range allows the iron-based amorphous alloy of the present invention to have excellent soft magnetic properties. In a specific embodiment, the content of B is 11.0 ≤ b ≤ 13.0, and more specifically, the content of B is 11.0 ≤ b ≤ 12.5.

In the present application, a preferred combination of the iron-based amorphous alloy is: a = 80.0, 12.0 ≤ b ≤ 13.0, 7.0 ≤ c ≤ 8.0; or a = 80.5, 11.5 ≤ b ≤ 12.5, 7.0 ≤ c ≤ 8.0; or 81.0 ≤ a ≤ 81.5, 11.0 ≤ b ≤ 13.0, 7.0 ≤ c ≤ 8.0.

The composition and content of the iron-based amorphous alloy provided by the present application are reasonably combined from the improvement of the magnetic induction intensity and the improvement of the amorphous forming ability, respectively, forming an iron-based amorphous alloy with high saturation magnetic induction strength, and further, having a high On the basis of the saturation magnetic induction intensity, the iron-based amorphous alloy of the present application also has low stress sensitivity; that is, the iron-based amorphous alloy provided by the present application has high saturation magnetic induction and low stress sensitivity due to the iron-based amorphous alloy. Adjustment of composition and content.

The application also provides a method for preparing an iron-based amorphous alloy strip as shown in formula (I), comprising:

The element is compounded according to the atomic percentage of the formula (I), and the raw material after the compounding is melted, and the melted molten metal is heated and kept warm, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip;

Fe _a B _b Si _c (I);

Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100.

In the process of preparing an iron-based amorphous alloy ribbon, the present application employs a conventional technical means in the art to prepare an iron-based amorphous alloy ribbon of the specific composition of the present application. The process of the ingredients and the smelting in the above preparation method is a process well known to those skilled in the art, and the specific operation means are not specifically described in the present application. In the smelting process, the metal raw material is smelted using an intermediate frequency smelting furnace, the smelting temperature is 1300 to 1500 ° C, and the time is 80 to 120 min. After the smelting, in the present application, the melted molten metal is heated and maintained, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip. The temperature for the temperature rise is preferably from 1350 to 1470 ° C, and the time of the heat retention is preferably from 20 to 50 min. After a single roll quenching, the present application obtains a completely amorphous iron-based amorphous alloy strip having an amorphous limit band thickness of at least 75 μm, and the strip toughness is good, and the sheet is folded 180 degrees continuously. For the purpose of the present invention, the shear limit band thickness is at least 29 μm, and the industrial production of the product has a considerable preparation margin, which reduces the requirements for the cooling equipment in the industrialization process.

After preliminary preparation of the amorphous iron-based alloy strip, the present application heat treats the amorphous iron-based alloy strip for ease of application. The iron-based amorphous alloy provided by the present application can realize a wide retreat The heat treatment is performed in the fire interval, and the obtained iron-based amorphous alloy strip has a low excitation power and loss. The temperature of the heat treatment described herein is 325 to 395 ° C; in a specific embodiment, the temperature of the heat treatment is 335 to 385 ° C.

According to the present invention, before the above heat treatment, the prepared iron-based amorphous alloy strip is preferably wound into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and the sample ring is subjected to heat treatment. Through the simulation experiment, the deterioration of the loss and the excitation power of the sample ring under heat treatment is detected by the simulation experiment, so as to explain the transformation of the properties of the iron-based amorphous alloy strip under stress state; if the strain coefficient is large Under the condition that the loss coefficient of the iron-based amorphous alloy strip and the deterioration coefficient of the excitation power are still within the acceptable range, it can be explained that the iron-based amorphous alloy strip has lower stress sensitivity, if the strain coefficient is even smaller. The loss coefficient of the iron-based amorphous alloy strip and the deterioration coefficient of the excitation power are still unacceptable, which indicates that the stress sensitivity of the iron-based amorphous alloy strip is poor. Through the simulation experiments of the present application, the experimental results show that the iron-based amorphous alloy ribbon of the present invention has low stress sensitivity.

The present invention reduces the stress sensitivity of the iron-based amorphous alloy strip by adjusting the content of the added component and the component, that is, the content of the component and the component synergistically to improve the magnetic properties of the iron-based amorphous alloy.

In order to further understand the present invention, the iron-based amorphous alloy provided by the present invention will be described in detail below with reference to the examples, and the scope of the present invention is not limited by the following examples.

Example

1) Preparation of iron-based amorphous alloy strip

According to the alloy composition represented by Fe _a B _b Si _c , the alloy composition shown in Table 1 is prepared using industrial pure iron, silicon or boron iron; the alloy component has inevitable impurity elements such as C in addition to the main element. , Mn, S, etc. The materials of different components are sequentially added to the intermediate frequency induction smelting furnace with a furnace capacity of 100kg in the order of boron iron, silicon and pure iron (the melting temperature is 1300-1500 ° C, the time is 80-120 min); the molten steel is calmed. At the end, it is poured into the spray bag, and an amorphous ribbon with an amorphous bandwidth of 20 mm is prepared by a single roll planar casting method. During the tape making process, alloy strips with different thicknesses are prepared by adjusting parameters such as roll speed and liquid level ( The roller speed during the belt making process is 1000 to 1400 r/min, and the belt speed is controlled to be 20 to 30 m/s, and the liquid level is 200 to 300 mm.

2) Amorphous forming ability and saturation magnetic induction strength test of iron-based amorphous alloy ribbon

XRD was used to test the free surface of the different component strips until the strip was thick to amorphous. Table 1 shows the amorphous limit band thickness of each alloy component. The saturation magnetization values of each amorphous alloy strip were tested using VSM. The alloy composition was comprehensively evaluated by the strip amorphous forming ability and the saturation magnetic induction value. The maximum thickness of the strip can be determined according to the number of brittle points of the strip. The brittle point is evaluated by taking the length of the strip as the circumference of the crystallizer and cutting the strip along the length of the strip. The number of brittle points is not more than 2 The material can be sheared, and equal to 2 is considered to be the limit of the strip of the alloy component.

Table 1 Amorphous iron-based alloys with different compositions and their performance data sheets

Table 1 presents the different alloy compositions with corresponding amorphous limit band thickness, tape toughness limit band thickness, and saturation magnetic induction. Amorphous limit band thickness and tape toughness limit thickness are the alloy component tape making process Sexual considerations, the thicker the above-mentioned belt, the more stringent the requirements for the belt making equipment.

Under the same conditions, the amorphous limit band thickness of the alloy composition is thicker, and the amorphous degree of the strip is higher. Although Comparative Examples 1 to 4 have a relatively high amorphous limit band thickness, the maximum shearable thickness is 27 μm or less, which not only imposes more stringent requirements on the cooling strength of the belt making equipment, but also on the assembly efficiency of the core, and at the same time on the transformer. During assembly and operation, easy debris has buried the foreshadowing, which has increased the safety hazard of transformer operation. In addition, its saturation magnetic density is less than 1.57T, which makes the design of amorphous transformer narrow and narrow, which can not meet the design trend of high magnetic density of transformer. Comparing Comparative Example 6 with Examples 4 to 6, it can be seen that the same Fe content, the higher the Si content, the smaller the shear thickness.

Comparative Example 8～9 alloy amorphous saturation magnetic density is obviously high. This is expected by transformer design. The maximum shearable thickness is between 36 and 38μm. It has absolute advantage in iron core forming efficiency, but its amorphous limit band It can be seen from the thickness value that the amorphous forming ability is obviously insufficient, and the process conditions of the slanting line are not obtained, and the excitation power and loss are also affected.

It can be seen from Table 1 that the alloy compositions of Examples 1 to 11 have a good process directivity and a wide transformer design interval from the consideration of tape straightening and transformer design.

The strips having a thickness of 26 to 28 μm and a width of 30 mm in Table 1 were wound into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and the sample ring was subjected to stress relief annealing using a box annealing furnace. Annealing was carried out in an argon-protected atmosphere from 325 to 395 ° C with a 10 ° C interval and 1 h of incubation. The heat treatment process adds a magnetic field along the strip preparation direction with a magnetic field strength of 1200 A/m. The silicon steel tester was used to test the excitation and loss of the strip after heat treatment. The test conditions were 1.35T/50Hz and 1.40T/50Hz, respectively. The performance test results are shown in Table 2:

Table 2 Performance data of the examples and comparative examples after heat treatment

It can be seen from Table 2 that under the condition of 1.35T/50Hz, the loss values of Comparative Examples 1 to 3 and Comparative Examples 8 to 9 are too large, and the performance is above 0.12 W/kg; and under the condition of 1.4 T/50 Hz, Comparative Example 1 The excitation and loss of ~4 and 6 are significantly higher than 1.35T/50Hz, and are significantly larger than other samples at 1.4T/50Hz, which is mainly related to the low saturation magnetic density of the above samples. The excitation and loss of amorphous materials increase with the increase of magnetic density, especially the performance of excitation power. An amorphous material with a large saturation magnetic induction strength has a lower saturation magnetic induction material, which allows a larger working magnetic density, that is, operation at a 1.4T magnetic density exhibits relatively low excitation power and loss. Normally, Comparative Examples 8-9 are tested at 1.4T, and the performance will be better. However, because of its large performance at 1.35T, the 1.4T loss and excitation increase, resulting in a large performance at 1.4T.

Examples 1 to 11 exhibited excellent soft magnetic properties at 1.35/50 Hz and 1.450/5 Hz; the 1.35/50 Hz loss was within 0.11 W/kg, and the 1.4 T/50 Hz loss was within 0.15 W/kg.

3) Stress sensitivity test

The above studies mention that the amorphous material has a relatively low unavoidable loss value, and the amorphous material is deteriorated by the external stress after being assembled into an iron core. In this study, a stress model of amorphous ring was established to characterize the deterioration of the properties of amorphous products with different compositions after stress deformation, and the simulation of amorphous ribbons was assembled into a transformer. The iron core is subject to changes in stress properties.

Sample treatment: Select the amorphous ribbon as the composition of Table 3, and make a sample ring with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm. The sample ring is subjected to stress relief annealing using a box annealing furnace, and annealing is selected in argon. Conducted in a protective atmosphere. The sample tape prepared by different components is selected, and the sample ring is prepared according to the above requirements for heat treatment. The heat treatment temperature is 325-395 ° C, and the heat treatment is performed as a gradient every 5 degrees, the heat preservation time is 60-120 min; the magnetic field strength is 800-1400 A/ m. The optimum heat treatment performance of each component in the above heat treatment process was selected to test the performance deterioration of the strip after stress.

The application of stress is calculated by calculating the indentation distance of the circular strip. The feed rate of the sample loop is calculated according to the formula of the deformation coefficient, as shown in Fig. 1. Fig. 1 is a schematic diagram of the simulation test device without stress state of the sample loop, and Fig. 2 is applied by the sample loop. Schematic diagram of the simulation test device of the stress state; when the sample ring is applied with stress, the A plate is fixed, and the feed amount of the sample ring is given under the push of the push plate B, the sample ring is deformed by the stress, and the plate B is fixedly pressed to test the deformation condition. The loss P _{1 of the} material and the excitation power Pe ₁ were measured using a silicon steel tester at 1.35 T/50 Hz.

The initial sample ring (under the condition of non-deformation) has an inner diameter of D ₀ , the properties are P ₀ and Pe _{0 respectively} , and the inner diameter after deformation is D ₁ . The properties are respectively P ₁ and Pe ₁ , and the strain coefficient is defined as (D ₁ -D ₀ ). *100%/D ₀ , loss deterioration coefficient = (P _{1 -} P ₀ ) * 100% / P ₀ , excitation power deterioration coefficient = (Pe _{1 -} Pe ₀ ) / Pe ₀ .

Considering the difference between the selected performance and the allowable degree of performance deterioration after deformation, this experiment stipulates that the performance deterioration is within 50%, and the corresponding ring-shaped variable corresponding to the performance value is the maximum allowable deformation coefficient value of the corresponding component material.

As can be seen from Table 3, the best performance is slightly different due to the difference of the components themselves. The performance of Comparative Example 9 is relatively large, and the other performance values are basically in the same category. The heat treatment temperature is better than the compositional difference ranging from 345 to 385 °C. In the stress experiments, the best performance samples after annealing of each component were selected for stress sensitivity experiments.

Table 3 Table of the best heat treatment performance data of different components

Table 4 Data Table of Loss Value and Deterioration Coefficient under Different Strain Coefficients

Table 4 Data Table of Loss Value and Deterioration Coefficient under Different Strain Coefficients (Continued Table)

Table 5 Data Table of Excitation Power and Deterioration Coefficient under Different Strain Coefficients

Table 5 Data Table of Excitation Power and Deterioration Coefficient under Different Strain Coefficients (Continued Table)

It can be clearly seen in Table 4 and Table 5 that the iron-based amorphous alloy is affected by the stress and a certain degree of performance deterioration occurs, and the coefficient of performance deterioration increases as the deformation coefficient increases. Comparing the loss of each component and the excitation power, it is found that the deterioration of the excitation power significantly exceeds its loss. The excitation power allows a coefficient of deterioration of 6%, while the loss allows a coefficient of deterioration of 10%. That is to say, the external stress applied to the amorphous ribbon has a greater influence on the excitation power.

Comparing the comparative examples and the comparative examples, it was found that the coefficient of deterioration of the properties of the different components after stress was greatly different, and the loss of the amorphous alloy ribbon of Examples 4-6 and 12 to 13 allowed a strain coefficient of 10.0%, Examples 4-6 The excitation power of 12-13 is allowed to have a deterioration coefficient of 6%, considering the performance short board effect, the extensibility coefficient allowed by the embodiment is 6%; and the allowable strain coefficients of the comparative loss and the excitation power are 8% and 2%, respectively. The deterioration coefficient allowed by the comparative example is 2%; thus, it can be seen that the annealed amorphous ribbon embodiment resists Force sensitivity has a clear advantage, allowing for greater deformation while ensuring material performance is within acceptable limits.

The above description of the embodiments is merely to assist in understanding the method of the present invention and its core idea. It should be noted that those skilled in the art can make various modifications and changes to the present invention without departing from the spirit and scope of the invention.

The above description of the disclosed embodiments enables those skilled in the art to make or use the invention. Various modifications to these embodiments are obvious to those skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the invention. Therefore, the present invention is not to be limited to the embodiments shown herein, but the scope of the invention is to be accorded

Claims (13)

An iron-based amorphous alloy as shown in formula (I), Fe _a B _b Si _c (I); Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100. The iron-based amorphous alloy according to claim 1, wherein the iron-based amorphous alloy has a saturation magnetic induction of ≥1.60T. The iron-based amorphous alloy according to claim 1, wherein the atomic percentage of Fe is 80.0 ≤ a ≤ 81.5. The iron-based amorphous alloy according to claim 1, wherein said B has an atomic percentage of 11.0 ≤ b ≤ 12.5. The iron-based amorphous alloy according to claim 1, wherein the Si has an atomic percentage of 7.0 ≤ c ≤ 8.0. The iron-based amorphous alloy according to claim 1, wherein in the iron-based amorphous alloy, a = 80.0, 12.0 ≤ b ≤ 13.0, and 7.0 ≤ c ≤ 8.0. The iron-based amorphous alloy according to claim 1, wherein in the iron-based amorphous alloy, a = 80.5, 11.5 ≤ b ≤ 12.5, and 7.0 ≤ c ≤ 8.0. The iron-based amorphous alloy according to claim 1, wherein in the iron-based amorphous alloy, 81.0 ≤ a ≤ 81.5, 11.0 ≤ b ≤ 13.0, and 7.0 ≤ c ≤ 8.0. A method for preparing an iron-based amorphous alloy strip as shown in formula (I), comprising: The element is compounded according to the atomic percentage of the formula (I), and the raw material after the compounding is melted, and the melted molten metal is heated and kept warm, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip; Fe _a B _b Si _c (I); Wherein, a, b and c respectively represent the atomic percentage of the corresponding component; 79.5 ≤ a ≤ 82.5, 11.0 ≤ b ≤ 13.5, 6.5 ≤ c ≤ 8.5, a + b + c = 100. The preparation method according to claim 9, wherein the single-roll quenching further comprises: The iron-based amorphous alloy after the single roll quenching is heat-treated. The preparation method according to claim 10, characterized in that before the heat treatment, the method further comprises: winding a single-roll quenched iron-based amorphous alloy into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm. The allowable strain coefficient of the sample ring after heat treatment is 10.0%, and the allowable strain coefficient of the excitation power is 6%. The preparation method according to claim 10, wherein the heat-treated iron-based amorphous alloy strip has a coercive force of ≤ 3.5 A/m; and at 50 Hz, 1.35 T, the heat-treated iron The excitation power of the base amorphous alloy strip is <0.1450VA/kg, the core loss is <0.1100W/kg; at 50Hz, 1.40T, the excitation power of the heat-treated iron-based amorphous alloy strip is <0.1700VA /kg, core loss <0.1500W/kg. The preparation method according to claim 10 or 11, wherein the iron-based amorphous alloy ribbon is in a completely amorphous state, has a critical thickness of at least 75 μm, and a shearable limit strip thickness of at least 29 μm.

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